Titanium base alloys containing antimony



R. l. JAFFEE ET AL 2,796,347

TITANIUM BASE ALLOYS CONTAINING ANTIMONY June 18, 1957 Filed Nov. 23, 1953 COMPARATIVE STRENGTHENING EFFECTS or Al, 56 AND 50 l LLor ADDIT'IONS- To COMMERCIAL PUB/T) 77-.BASE

120 100 Al yr y A A QZPEE CENT OFFSET YIELD STRENGTH O 4 8 I2 16 2O 24 ADDED ELEMENT, WEIGHT PER cENr INVENTORS. R0 BERT [.JA FFEE. HORACE R. OGDEN. By RALPH A. HA PPE.

I MMQM ATTO/F/VEKS'.

United States Patent TITANIUM BASE ALLOYS CONTAINING ANTHVIONY Robert I. .Jaflee, Worthington, and Horace R. Ogden, Columbus, Ohio, and Ralph A. Happe, Anaheim, Calif.,

assignors, by mesne assignments, to Rem-Cm Titanium Incorporated, Midland, Pa., a corporation of Pennsylvaula Application November 23, 1953, Serial No. 393,578

12 Claims. (Cl. 75175.5)

This invention pertains to binary alloys of titanium and antimony and also to ternary and higher component alloys formed therewith by additions of other elements including alpha-promoting, beta-promoting and compound-forming elements.

This application is a continuation-in-part of our copending applications Serial No. 327,421, filed December 22, 1952, and Serial No. 371,112, filed July 29, 1953, now abandoned. i

The alloys of the invention are in general characterized by excellent mechanical properties, possessinghigh tensile strength as compared to the unalloyed titanium-base metal, combined with adequate ductility for both hot and cold forming operations, i. e., forging, rolling, etc. alloys of the invention may be welded without appreciable loss of ductility in the welded as compared to non-welded portions. And the same is generally true of the ternary and higher component alloys as shown by the test data set forth below. The alloys of the invention also have good contamination resistance as regards oxidation and penetration by atmospheric gases at room and elevated temperatures.

The binary titanium-base alloys of the invention are quite ductile throughout the range of about 1 to 18% Sb. Higher antimony additions result in increasing embrittlement, but are useful in cast form for antimony additions up to about 25%. The ductile Ti(1-18%)Sb base alloys are greatly strengthened without appreciable loss of ductility by additions of limited and controlled amounts of the interstitials, carbon, oxygen and nitrogen. To this end, carbon may be present up to about 0.6%, oxygen up to about 0.4% and nitrogen up to about 0.3%. Further strengthening with retention of adequate ductility results from additions of other elements, including alpha-promoters, beta-promoters and compound-forming elements, as enumerated and in proportions as set forth The binary I 2,796 ,34 7 Patented June 18, 1957 body-centered cubic structure known as the beta phase.

I Certain substitntional alloying additions to the titaniumbase metal, among which may be mentioned aluminum, indium, bismuth and lead, as well as the interstitials'carblon, oxygen and nitrogen, tend to stabilize thev alpha p ase.

Our investigations with iodide-base titanium-antimony alloys have shown that antimony has a slight beta stabilizing tendency in that the transformation range shifts progressively' downward to about 840 C. as the antimony content is increased to the terminal alpha solubility of about 17.5%. It should be emphasized, however, that antimony has thus a relatively indifierent effect on the transformation temperature of titanium. It produces allalpha alloys with titanium which undergo no hardening on quenching from the beta field. Antimony may thus be considered an alpha stabilizer, and it will be so treated in the following.

Tin behaves in a manner quite analogous to antimony and likewise should be treated as an alpha stabilizer.

' Silver, formerly considered an alpha stabilizer, now appears more properly grouped similarly to tin and antimony. The effect of silver on the transformation range-is so slight that silver may be considered as either an alpha or beta stabilizer, and it will be treated as an alpha stabilizer in the following.

Other substitutional alloying elements, when added in progressively increasing quantities, stabilize the beta phase at progressively lower temperatures, until a mixed alpha-beta or stable all-beta microstructure is obtained at normal or atmospheric temperatures, or the beta phase undergoes a eutectoid reaction, depending on the character and amount of the beta stabilizers added.

Speaking in broadest terms, the beta stabilizers are Mo, V, Cb, Ta, Zr, Mn, Fe, Cr, W, Co, Ni and Cu; Silicon and beryllium may also be considered as beta stabilizing elements, but their solubilities in titanium are relatively small, so that it is equally proper to consider them as compound-forming elements. Within this broad category, however, only certain of the elements mentioned are suitable for producing mixed-phase, alpha-beta alloys, or allbeta alloys. These are the elements which have beta-iso- 3 morphous diagrams, or which have beta-eutectoid diagrams such that the decomposition of the beta phase into eutectoid is so sluggish that the alloys behave like those in a beta-isomorphous system. The beta stabilizing elements of this type are Mo, V, Cb, Ta, Mn, Fe, Cr and W. Within this group only Mo, V, Cb and Ta are beta-isomorphous. They form the. most thermally stable betacontaining alloys, as a result of their beta-isomorphism.

Zirconium is a beta promoter or stabilizer in the sense that the lowest temperature at which alloys thereof with titanium are entirely beta, becomes progressively lower with increasing amounts of zirconium, until a composition is reached at which this so-called beta transus temperature starts to increase again with further additions of zirconium. While zirconium thus lowers the transformation temperature of titanium, the alloys eventually revert to the alpha phase at lower temperatures unless other beta-promoters are present. Zirconium isisomorphous with titanium both in the alpha and beta fields: As a result, itis proper to consider zirconium together with vanadium, molybdenum, columbium and tantalum'as all being beta-isomorphous with titanium. I

The use of copper alone as an alloying addition to titanium, does not fit into the above-mentioned grouping of beta-\isomorphous and sluggishly decomposing eutectoid beta promoters, because the beta phase stabilized by copper always decomposes rather rapidly into pro-eutectoid and eutectoid products, and the same is generally true with respect to cobalt, nickel, silicon and beryllium, above listed under the broad category of beta stabilizers. Copper, however, is a useful addition when present as a minor alloying element, for example, up to a few percent, in alloys containing larger amounts of other beta-stabilizing elements, within the limited group of beta-promoters last mentioned above since, in these low concentrations and in the presence of such other beta-stabilizing elements, the tendency of the beta phase stabilized in part by copper to decompose into eutectoid products is minimized or entire- 1y eliminated.

The tolerance of the TiSb base alloys of the invention with respect to additions of the various beta-promoters above mentioned, varies considerably for the individual elements of this group, being greatest with respect to those which form beta-isomorphous systems with titanium, and least for those which decompose most readily into eutectoid decomposition products. Thus, the Ti- Sb base alloys may be strengthened without undue embrittle-.

ment by additions of up to about 40% or even up to 50% in aggregate of elements composing the beta-isomorphous group, viz., molybdenum, vanadium, columbium, tantalum and zirconium. Of the sluggishly decomposing elements, the base alloy will tolerate additions of up to about 25% of either or both chromium and tungsten, up to about 10% manganese, and up to about 7% iron. Metal of the group cobalt, nickel and copper may be added up to a total of about For additions of all of the abovementioned beta-promoters, the lower efiective limit is about 0.5% and preferably about 1%. In all of the alloys in this category, the antimony content should be on the low side of its range when the beta-promoter addition is on the high side of its range and vice versa.

The tolerance of the Ti-Sb base alloys for the alpha promoters depends on the amount of antimony present, the less antimony present the greater the amount of alphapromoters that can be added, and vice versa. Aluminum maybe added to a maximum content of 8%, and tin may be added to a maximum content of 22.5%. The proportioning of aluminum at the high antimony contents and of tin are given subsequently. Indium and silver may be added up to a maximum content of 15 Lead and bismuth may be added up to 15% added to the charge in melting.

The elements Ce, B, As, S, Te and P are strictly compound-forming elements. They do not have appreciable solubilities in either the alpha or beta phase, but form intermetallic compounds with titanium. The beta promoters silicon and beryllium are likewise best grouped as compound-forming elements, in view of their abovementioned low solubilities in titanium. The TiSb alloys of the invention will tolerate only relatively small amounts of these compound-forming elements, i. e., up to a total of about 2% maximum, the lower effective limit being about 0.1 or 0.2%.

Substantially pure and ductile metallic titanium may be produced at considerable expense by the so-called iodide process described in U. S. Patent 1,671,213 to Van Arkel; while ductile titanium of commercial purity is produced more cheaply by the magnesium reduction of titanium tetrachloride by the process described in U. S. Patent 2,205,854 to Kroll. Both procedures, particularly the latter, result in some contamination of the titanium metal with one or more of the interstitials, carbon, oxygen and nitrogen. But since, as noted above, these are all alpha-promoting or stabilizing elements, the resultant somewhat contaminated titanium metal obtained, has at room temperatures a single phase, all-alpha microstructure.

The all-alpha, all-beta and mixed alpha-beta alloys of titanium have their respective advantages and disadvantages. Generally speaking, the alpha alloys provide good all around performance, having good weldability, and being strong and resistant to oxidation, both cold and hot, but are somewhat inferior as to ductility. The all-beta alloys, on the other hand, have excellent bendability and ductility, are strong both hot and cold, but are somewhat vulnerable to atmospheric contamination, particularly at elevated temperatures. The mixed alpha-beta alloys provide a compromise performance as between all-alpha and all-beta alloys, being strong when cold and warm, but weak hot, While possessing good bendability and ductility, with a moderate degree of resistance to atmospheric contamination.

The following Table I gives the mechanical properties of. the binary alloys of antimony and iodide-base titanium over the ductile range of about 118% Sb. The succeeding Table II gives the corresponding values for the binary alloys of antimony and titanium-base metal of commercial purity. This table also shows the strengthening effect of additions of the interstitials carbon, oxygen and nitrogen.

Referring to Table I, it will be seen that additions of up to about 18% antimony to iodide-base titanium more than trebles the yield strength and approximately trebles the ultimate strength with retention of adequate ductility for fabrication purposes. The yield strength increases from 24,000 p. s. i. to upwards of 80,000 p. s. i., and the ultimate strength increases from 40,000 to about 100,000 p. s. i., while retaining the minimum bend ductility at values under 4T, and the percent tensile elongation at values of upwards'of about 15%.

Referring to Table II, for the commercial purity titanium-base values, the yield strength is more than doubled by additions of antimony up to about 18%, the yield strength increasing from about 48,000 to about 110,000 p. s. i., and the ultimate strength from about 71,000 to about 120,000 p. s. i. As further shown by the test data, the binary alloys become somewhat embrittled above about 16% Sb, although they can still be fabricated. Additions of the interstitials further enhance the tensile properties while reducing the ductility but slightly. Thus I V TABLE I Mechanical properties of iodide titanium-base Ti-Sb alloys 2 7 [These alloys were 980 0. forged, 850 0. rolled to 0.04" and annealed 2 hours at 850 0.

ing.Tab1e III, showingithe efiectiiof de when 3111- V I v minum is on the high side of the aforesaid ranges and vice The foregoing conclusions are based on the test results;

in the fo1l0w m r g m 0 l m f m v. y t 10 mm? 000500 m mmm R6451 H 11111 m h 2 a S s .1 m n 5 f. e 200000 m mm eLzs 4 5 m c n 1 11 TB. 0 n 3 3 8266866540r 4.708 m o I -01221 e I u l -B l m m 1 Tr T 0111212267 @2454 1 g o R MA m m m 2 1 B 842585655rr 5054 m m 1 m M L 1 0 0 LLLL2 2 2 \L&22 .W o Td 00179322 H- 8 1 1 1 v u T LLL2.3.3.H\ m HM 79277774120 8869 5 0 mm 00662441, r H m m mumnnwwmmmwwmwnw e 7 .1 ,a ,1 1, M L 011233@ Y .m rm V m.mmmm mm mm.w 2 1 H mm muwwwnn a mwnm mm gee n m c m HM m a 5 1 6 S 3 6 en 11111222 r 1 d0 1 r I mm 1 W 2 mmmm wmwawc mw n w 1 vm 2 2 we emiwmm mm S d n w I 15520915024 876 1 O O t m t 1 mw m nuw weww m m m mms f 2222211111 11 Ym mm mmmr mf m w m mmmA 1 w H m m m f td iw w R2 11 m PE m wmm o c r i E 1 e d s b m 1 1 1 3 0 o m. mmmmm mmmm m m w 2 I 1 e 1 my? 2 Man mm, m o mwmemwwwmeme m em m T a n1 m s P m.m.m PE we m 2 mmom ium m a e 1 P e 6 nd S 0 g 1 8 181709459 4731 7 m m mm hee mm a m m 7 mm 4eiggnnm mnnm wmim mm m m .fi 0 1 n 0 P 6 w M. ED 0 6k t I 1 O 0v a P 2 m x mw 1 w 1. T w m m eme 1 m 1 m M zMfmsmmmim t 4 224662 a a 0 E C 1.2.010 "me w 2%345688 n .w m m .md s%.w%fipm1m.w VZW m 0m m .m w e w m w wtm mm 9 h W. P f. a e 0 a C V. e m w w m mm m uot mlwsmrm m m wm m M H me m sw jy m mmmm Q m n d s fi n .O p c fl2w w m on d 6 0. I n 6 d we? 2 m 1 m m efifi m. w l '1 o T 0 mm o .m m hemm 0 1 1 fle fimm m unm% Id t PW w afiS mony, the antimony being on the low si versa. The preferred maximum antimony content for a 75 given.

the Ti% Sb alloy increases the yield strength by about and the ultimate strength by about 20%, or from 48,000 to 80,000 p. s. i. for the yield strength and from purity base alloys of Table II are plotted against the anti- .mony content, and the same is done for the .Ti..A1 commercial purity binaries,-as shown'in the accompanying drawing, it will befound that to a close degree of approXirnation,"1% of aluminum is equivalent to about 3% of either antimony or tin, as regards strengthening efi ect,

The data in Table III illustrates that thisequivalency holds approximately in'ternary .Ti.-Al.-Sb alloys.

.TABLE III -Mechanical properties'bf Ti-Sb--Al alloys (commercial purity Ti-base) [These alloys were 980 0. forged, 850 0. rolled and annealed 2 hours at 850 9,]

Tensile Properties: MBR, '1

p. s. i. 1,000 Percent Percent Composition; Percent Elonga- Reduc- Vickers' (Balance Titanium) tion in 1 tion in Hardness 0.2% 011- Ultimate Area L '1 set Yield Strength 53 77 22 202 0. 7 1. 8 112 120 15 32 345 2. 4 3. 1 20 40 351 2. 7 2. 7 118 124 17 33 352 3. 5 3. 4 121 126 15 39 355 3. 4 2. 5 122 15 44 360 3. 5 2. 6 58 77 22 47 227 1. 5 1. 6 80 91 16 42 262 2. 1 2. 2 92 i 96 12 46 288 1. 5 2.0 96 102 15 49 311 2. 1 2. 1 104. 111 19 46 323 2. 8 2. 6 118 124 17 33 352 3. 6 3. 4 121 126 15 39 355 3. 4 2. 5 128 129 15 40 336 5. 0 3. 3 71 86 20 49 257 1. 8 2. 8 121 124 16 '39 '355 2; 8 3. 8 77 91 19 46 267 1. 5 1. 6 104 108 18 48 298 2. 1 1. 9 119 121 12 43 342 2. 5 3.1 128 132 9 37 350 '2. 8 3. 6 130 131 13 28 376 2. 5 2. 5 144 144 8 29 356 Br 12.5Sb 90 101 11 48 277 2. 6 2.6 12.5Sb-1Al- 114 120 20 41 312 2. 1 4.0 12.5Sb-2Al. 128 128 8 38 353 2. 3 4. 0 12. 5Sb-3AL 135 138 6 28 355 Br Br 12.5%-41H- (0 0) (0 15Sb 99 111 15 43 304 2. 5 2. 5 15Sb-1Al. 127 131 12 46 342 3. 1 3. 8 15513-2111.. 139 142 8 37 345 'Br 5. 3 l5 b3A1- 17Sb 115 124 12 32 322 Br 7. 0 17.5Sb1Al 144 5 27 338 Br Br 17.5Sb-2A1 1 Could not be fabricated. 3 Too brittle for testing.

77,000 to 91,000 p. s. i. for the ultimate strength, without impairing the ductility in any appreciable degree, the minimum bend ductility being about 2.2 T and the percent tensile elongation about 16%. Further strengthening of the Ti5% Sb alloy results from additions of up to 3% aluminum, the yield strength being thus increased to 96,000 and the ultimate strength to 120,000 p. s. i., while still retaining substantially the same ductility, i. e., about 2 T for the minimum bend and about 15% for tensile elongation. Corresponding enhancements in tensile strength with retention of adequate ductility result from additions of up to 4% A1 to the Ti-10% Sb base alloy, the yield strength increasing from 77,000 to 130,000 p. s. i. and the ultimate strength from 91,000 to 131,000 p. s. i., the minimum bend increasing to only 2.5 T. About the same strengthening enhancements result from additions of up to about 3% Al to the 12.5% Sb base alloy, and up to about 2% A1 to the 15% Sb base alloy, and up to about 1% A1 for the.17..5% Sb base alloy, consistent with retention of adequate ductility for purposes of fabrication.

l the tensile properties for the Ti-Sb, commercial As shown in the copending joint application of W. L. Finlay and the applicants Iaifee and Ogden herein, Serial No. 341,796, filed March 11, 1953, the upper limit for additions of tin to titanium which can be fabricated, is about 23%. Correspondingly, it is shown in the present application that the upper limit for additions of antimony to titanium which can be fabricated, is about 18%. The following Table IV gives .test data establishing the upper limit for combinations of titanium, tin and antimony. Thus from the data of Table IV, it will be seen that the maximum amount of tin that may. thus be added to the Ti-Sb base alloy, for any given percentage of antimony present, is as set forth'in the following tabulation:

Percent Percent Antimony Tin; Max.

TABLE IV Mechanical properties of Ti-Sb Sn and (Commercial purity Ti-bases) [These alloys were 980 C. forged, 850 0. rolled and annealed two hours at 850 0.]

Tensile Properties: MBR, T p. s. i. 1,000 Percent Percent Vickers Composition, percent (Balance Elon- Reduc- Hard- Titanlum) gation tion in ness 0.2% 06- Ultimate in 1" Area L '1 set Yield Strength 1 (9 111 3 304 2. 5 3.3 o 6 ai (e 91 19 46 267 1. 5 1. 6 96 16 46 268 2. 3 3. 1 94 17 46 262 1. 5 4. 7 98 18 43 270 2. 2 3. 2 92 46 278 1. 7 2. 1 111 15 43 304 2. 5 2. 5 117 14 42 311 1. 9 3. 7 111 17 44 317 2. 5 3. 2 116 17 39 325 1. 7 3. 5 118 14 36 313 2. 9 5. 5 117 16 348 1. 8 2. 7 125 13 38 351 2. 4 3. 3 115 15 48 339 2. 6 3. 4 118 13 44 343 2. 8 3. 6/5. 2 117 15 40 345 2. 6 2. 5 119 20 43 345 2. 5 3. 2 146 16 47 393 2. 0 2. 8/31 137 8 24 402 2. 8 2 7 5. 3 157 5 18 400 6. 2 Br 146 5 21 390 3.0 5. 2 141 6 29 395 5. 5 Br 117 15 42 352 2. 8 2. 7/5. 3 109 15 43 351 2. 8 3. 7 113 15 37 346 2.1 8. 6 5Al-1Sb-L5Sn--- 112 17 46 343 2. 9 7. 6 5Al-0.5Sb-2Sn 100 111 14 43 348 2. 8 2. 7 5A12.5Sn 101 110 17 47 344 2. 9 2. 7 5Al2.5Sb-0.20.. 128 134 7 21 389 2. 8 7. 6

5Al-2Sb-0.5Sn-0 5Al1.5Sb1Sn0.20 132 135 17 42 394 2. 8 3. 5 5Al-1Sb1.5S11-0.20 131 135 17 48 396 2. 8 2. 8/5. 6 5Al-0.5Sb-2Sn0.20 130 134 7 28 391 2. 8 2. 8/5. 5 5A1-2.5Sn-0.2G 134 135 9 25 400 2. 8 6. 8

1 Could not be fabricated.

The data in Table IV also establishes that tin is equivalent in strengthening eifect to antimony when substituted therefor on a weight percentage basis, i. e., percent for percent. Thus it will be seen that for the series of alloys starting with Ti10% Sb, in which Sn is progressively substituted for Sb at values of 2.5, 5, 7.5 and 10%, the yield and ultimate strengths remain substantially constant at about 74,000-77,000 p. s. i. and 92,000-98,000 p. s. i., respectively. Likewise for the corresponding series starting with Ti-l5% Sb, the yield and ultimate strengths remain substantially constant at about 100,000- 109,000 and 111,000-117,000 p. s. i., respectively.

The data in Table IV thus establishes that a substantially direct equivalency exists between tin and antimony additions for TiSnSb alloys. In Ti-Al(Sb, Sn) alloys the preferred maximum antimony content for given aluminum and tin contents is shown by the following relationship:

If the tin content is higher, the maximum antimony content is lower, and vice versa, in accordance with the equivalency between tin and antimony. However, for TiAl(Sb, 'Sn) alloys without carbon additions, the data indicates a trend toward higher strength when no tin is present in the alloys. This is shown by comparison of the values for the series of alloys starting with Ti10Sb-2.5Al and ending with Ti--10Sn-2.5Al. For the first alloy of the series containing no tin, the yield and ultimate strengths are 123,000 and 125,000 p. s. i., respectively, while for the remaining or tin substituting alloys of the series, the yield and ultimate strengths are lower, in the range of 110,000-114,000 and 115,000- 119,000 p. s. i., respectively. This same holds true for the series commencing with Ti-5Al2.5Sb in which tin is progressively substituted down to T i5Al-2.5Sn. For the first or non-tin containing alloy of the series, the yield and ultimate strengths are 110,000 and 117,000 p. s. i., while for the tin-containing analyses, the corresponding values are 101,000-103,000 and 109,000- 113,000 p. s. i., respectively. On the other hand, when carbon is present in these aluminum-containing alloys, there appears to exist a direct equivalency between tin and antimony as shown by the further data in Table IV for the alloy series starting with Ti10Sn2.5A1-0.2C and Ti--5Al2.5Sb0.2C, respectively.

Although as stated, 1% Al is roughly equivalent to 3% Sb in strengthening effect, the data indicate that the "I1 highest yield strengths for a given total equivalent alloy content in TiSbAl alloys, are obtained when the antimony-aluminum ratio is :1; whereas in the TiSnAl alloys, the strengthening effects of aluminum and tin are approximately additive based on a 3:1 ratio of equivalency of tin to aluminum. The significance of this is that an extra 5 ,00010,000p. -s. i. of tensile strengthening can be obtained by using the '5 :1 ratio of antimony to aluminum in ternary TiSbAl alloys over what can be obtained in the equivalent TiSn'Al ternary alloys.

The following Table V shows the efiect on mechanical properties of additions of other alpha promoters, as well as beta promoters and compound formers to the TiSb base alloys of the invention. With respect to additions of beta promoters of the beta isomorphous group, additions of up to molybdenum are shown to result in a tremendous enhancement in tensile strengthwhile retaining the alloy in extremely ductile condition. For the Ti4% Sb base alloy, the tensile strength is approximately doubled by additions of up to 12% molybdenum while maintaining the minimum bend ductility under 2.8T. Similar results are obtained for corresponding-additions to the Ti(812%) Sb base alloys. These same remarks are likewise applicable to additions of the remaining elements of the beta isomorphous group to the base 12 alloy i. e., vanadium, columbium and tantalum. In each instance there is a markedenhancement in strength with practically no loss in ductility. With respect to the eutecttoid beta promoters, those which are sluggishly reactive, such as iron, manganese and chromium, greatly strengthen the, alloy without unduly embrittling the same.

Thus, for example, the'addition of up to 5% iron to the Til0% -Sb base alloy, increases the ultimate strength from 101,000 to 159,000 p. s. i., while maintaining a minimum be'n'd ductility of not over 4.3T. About the same strengthening effect results from corresponding manganese and chromium additions with no loss in ductility. Thus the addition of up to 4% chromium to the Ti10% Sb base, increases the ultimate strength from 101,000 to 143,000 p. s. i., while retaining the bend ductility constant 'at 1.7T. The addition of up to 8% manganese to the Ti-8% Sb base increases the ultimate strength from 88,000 to 157,000 p. 's. i., while retaining a bend ductility of not'over 2.6T. As regards the rapidly decomposing 'eutectoid beta promoters and the compound formers such as silicon, boron, arsenic, 'etc., the strengthening action is not so great, andlikewise these elements when present in appreciable amounts, are decidedly niore embrittling in their effect.

TABLE V Mechanical properties of Ti-Sb base alloys plus additions of alpha promoters, beta promoters and compound formers (Commercial purity Ti-base) [These alloys were 1800 F. forged, 1400 F. rolled to 0.1, descaled, 1300 F. rolled to 0.040, held 15 minutesat 1300 F., furnace cooled to 1100 F., held 1 hour at 1100 F., air cooled to room temperature (stabilizing treatment) Tensile Properties: MBR, T

p. s. i. 1000 Composition, Percent (Balance Percent Percent Titanium) Elonga- Reduc- Vickers 0.2% Ultimate tion in 1 tlon in Hardness Ofiset Strength Area L T Yield '120 121 10 32 248 1. 5 1. 4 108 6 37 207 1. 3 2.8 68 80 20 51 180 1. 6 1. 4 118 120 4 22 255 1. 7 2.8 121 122 6 268 1. 3 2. 7 78 88 20 53 206 1. 8 1. 8 110 118 19 47 272 1. 8 2. 7 109 118 13 43 263 1. 7 1. 8 118 125 9 32 273 1. 8 1; 8 113 136 7 22 305 1. 5 2. 6 128 133 6 24 279 0. 4 1. 8 129 133 8 33 333 1. 5 2. 3 126 130 12 30 287 0 0 101 108 19 47 235 2. 7 2. 6 133 135 9 11 292 2. 4 4. 9 142 146 7 299 2. 7 3. 5 142 145 7 29 299 1. 3 2. 6 112 115 11 31 272 1. 2 1. 6 117 118 5 40 281 1. 5 2. 9/5. 8 68 20 51 180 1. 6 1. 4 120 124 8 36 285 1. 8 3.0/6.0 124 131 8 27 287 '2. 1 6. 8 78 88 20 53 206 '1. 8 1. 8 111 18 55 317 2. 3 2.0 126 15 45 319 1. 8 1. 9/3. 8 120 126 8 35 294 0.5 2.1/5.7 130 144 6 41 306 2.3 4. 5 130 144 7 33 309 2. 6/7. 1 Br 129 11 41 323 1. 6 4. 7 125 131 6 26 305 2. 4 5. 4 95 101 17 51 227 1. 7 1. 8 129 14 48 336 2. 7 2. 7 133 138 7 41 336 2. 2 1. 6 138 143 6 38 333 1.8/5. 2 5. 5/Br 117 117 17 45 327 1. 5 1. 9 126 131 10 28 318 2.0 4. 9 96 111 18 43 275 1.0 0. 9 107 117 10 39 277 0. 7 1. 6 105 115 8 28 290 0. 9 10. 5 93 110 20 50 288 1. 5 1. 6 94 119 19 45 280 1. 4 1. 8 97 123 1.6 35 268 1. 2 6. 4 111 116 18 45 315 2. 7 2.8 138 141 7 31 321 .1. 1 2. 8 123 12 28 293 l. 8 2. 9 126 126 12 50 338 11. 3 2.8 141 142 12 40 342 2. 4 2. 7 42 59 28 50 1. 4 1. 3 93 105 15 24 270 1. 6 1. 7 116 132 19 50 318 1. 6 2. 4 68 80 20 51 1. 6 1. 4 106 123 18 39 319 2. 5 5. 7

14 TABLE V-Co'r'ifinued Mechanical properties of Ti-Sb base alloys plus addi tions of alpha promoters, beta promoters and compound formers (Commercial purity Ti-base)Con.

Tensile Properties: MBR, T

p. s. i.X1000 V Composition, Percent (Balance Percent Percent Titanium) Elonga- Reduc- Vickers 0.2% Ultimate tion in 1" tion in Hardness Offset Strength Area L '1 Yield 123 142 14 26 332 2. 2. 5 78 88 53 1. 8 1. 8 116 134 14 23 322 2. 0 2. 4 129 144 16 29 338 1. 0 2. 4 95 101 17 51 1. 7 1. 8 124 V 125 20 46 337 2. 4 2. 0 126 131 19 V 31 330 2. 5 2. 5 131 143 9 5 343 1. 7 1. 5 140 144 11 a 26 316 5. 1 101 v 108 19 V 47 2. 7 2. 6 123 124 V 16 44 353 1. 5 3. 5 142 148 15 47 345 3. 7 2. 5 135 144 15 354 2. 5 2. 5 135 147 13 17 358 1. 7 2. 4 114 116 12 48 2. 5 2. 6 142 142 V 15 350 9.4 4.7 139 153 V 12 26 358 2. 3 2. 3 93 1 112 V 20 273 1.3 1.4 113 V V 126 V .V. 19 42 322 2.0 1.5 112 133 V 20- 32 337 1. 1 2. 1 V 88 V 20 47 191 1.3 0.9 100 116 V 20 45 301 1.3 1.3 118 132 20 31 318 1. 1 1. 5 123 142 13 28 347 0.8 2. 5/10. 0 68 .V 20 51 180 1. 6 1. 4 104 ..V. 13 31 298 1.8 1. 1 111 127 12 26 329 1. 1 1. 7 118 137 13 30 330 1. 5 2. 0 126 142 13 31 345 0.8 3.8 74 85 V 21 57 192 1. 6 1. 4 104 V 116 V 15 41 321 1. 6 1. 5 118 132 V 15 33 328 1.5 2.1 132 146 V 8 22 356 1. 3 2. 2 139 153 V 12 23 358 1.2 2.7 .78 88 20 Y 53 206 1. 8 1. 8 104 V 18 43 325 2. 8 1. 8 108. V 18 43 334 2.8 2.7 115 V J 15 29 330 2. 7 2.3 129 137 10 30 345 1. 7 1. 7 138 148 11' 27 362 1. 5 2. 6 146 157 10 25 360 1. 2 2. 6 95 101 17 51 227 1. 7 1. 8 119 123 16 44 342 2. 6 1. 8 133 12 43 328 1. 5 139 150 15 20 362 1. 7 2. 6 153 13 30 372 1. 4 3. 8 101 108 19 47 235 2. 7 2. 6

121 128 16 V 39 336 2. 7 2. 7 119 126 19 36 352 3. 1 2. 5 141 15 37 350 1.7 2.2 144 153 13 29 354 1. 9 2. 6 114 116 12 48 238 2. 5 2. 6 134 135 15 26 356 2. 9 2. 5 144 148 V 14 27 372 5.1 2.6 71 98 18 I 45 249 1.5 2.2 70 88 20 47 191 1. 3 0.9 132 134 0 5 356 10. 0 10. 1 68 80 20 51 180 1. 6 1. 4 113 136 8 16 338 9. 3 11. 0 74 85 21 57 192 1. 6 1. 4 102 20 44 300 2. 8 2. 3 139 157 9 19 372 8. 4 7. 5 78 88 20 53 206 1. 8 1. 8 114 126 18 37 333 4. 1 1. 8 131 144 4 8 361 6.1 4.0 95 101 17 51 227 1. 7 1. 8 115 121 15 39 337 2.8 2.7 118 128 12 21 348 7. 7 4. 2

16 TABLE V-Continued [The following alloys were 1,800 F. forged, 1,400" F. rolled to 0.1, (16362166, 1,400 F. rolled. to 0.04, annealed 15 minutes at 1,400 F. or at 1,550 F the latter as indicated by an asterisk, and quenched (beta fabrication treatment) V Tensile Properties: MBR, T

p. s. i. l000 Composition, Percent (Balance Percent Percent Titanium) 7 Elonga- Reduc- Vickers 0.2% Ultimate tioninl" tionin Hardness Ofiset Strength Area L T Yield 125 126 6 36 343 1. 1. s 69 110 8 26 251 1.0 1.0 115 130 287 0 0.5 123 10- 37 276 0 0 117 122 7 39 260 0 0 119 123 V8 38 268 0 0 121 6' 33 266 0 0 116 118 1 0 312 ogl. 9 0) 7120 1 0 V Br V Br 131 142 .1 3 312 5. 8/Br 7. 2 129 138 5 28 314 2. 8/Br 3. 1/6. 0 164, 166 1 o 386 V Br 7. 3/v Br 144 5 29 317 1.9 1.9 137 144 .4 t 27 306 1. 9/5. 7 3.0 148 6 24 326 2. 5/4. 9 6. 1 150 1. 2 350 5. 7/Br VBr 133 133 8 33 296 0. 9 0. 9 103 108 12 30 236 0 0.9 111 115 10 33 256 0 0.5 '68 s5 14 23 203 0. 5 1. 0 69 100 14 28 209 0.5 109 142 5 6 308 6.0 5.3 189 190 3 10 423 3. 5 7. 8 140 145 10 27 336 0 0 141 150 10 26 336 0 0 139 '6 11 337 0. 9 2. 1 149 157 5 10 350 1. 8 6. 1 136 150 6 24 346 0. 9 1. 7 v135 144 14 31 335 1. 2 1. 6 147 154 3 6 360 4.2 Br 1 ,137 .144 8 33 323 0. 4 1. 2 8Sb-120r 142 143 9 32 323 0. 4 1. 3

I Could not be fabricated.

Referring to the above table, it will be seen that the TABLE VII Ti-Sb-(Mo, V, Cb, Ta) alloys when given the stabilizing treatment, have very similar properties. On the 45 Bend dummy f q f 5 7? Tl sbsn and other hand, when these alloys are given the beta fabncaa 3' tion treatment, the TiSb-V alloys are shown to have (IODIDE Ti BASE) higher strengths and much lower ductilities than the corresponding TiSbMo alloys. Mllfiigliltlllg 11 116 The following Table W gives elevated temperature test 50 Composition, Percent (Emma Titanium) results on oxidation and contamlnation resistance of Welded Not alloys according to the invention: welded TABIJE VI 8 0.6 Oxidation data for T1-'Sb alloys 1.3

[Heated 4 hours at 1050 C. in air and furnace cooled] 3.7

W h Mliletaltil lepth of lrrcrnelaes 0 com osition, Percent eig t '1 ie ontamin (Balgnce Titanium) Gain, ness ination, mils below (COMMERCIAL PURITY T1 BASE) g./d!n. Loss, mils surface 111115 1.5 0.8 2.3 0.4 3. 45 10 60 210 i g 4.72 5 60 200 4.35 4 40 110 7. 00 7 Nil Nil 9 5 5.0 2.5 i t .3 r From the above it will be seen that these alloys are quite V Br Br resistant to oxidation and to penetration by atmospheric 2 1 2 gases at temperatures as high as 1050 C. 6.6 1.7 The following Table VII gives data on the weld ng $3; characteristics of alloys in accordance with the lnven- L5 tion as are welded in an inert atmosphere, in this case, 5- 2:3 argon. V Br Br TABLE VIIQContinued, g V TABLE Vil -Continued Bend, ductility of welded Ti- -Sb, Ti-.-Sb-Sn and Bend ductility of welded Ti-Sb, TiSb--Sn and Ti-Sb- Al' alloys- Continued Ti-Sb--A1 alloys- -continued (COMMERCIAL PURITY Ti BASEy continued 5 (COMMERCIAL. PUBITY Ti;BASE).-Continued Minimum Bend I Minimum Bend Radius, '1 Radius, '1 Composition, Percent (Balance-Titanium) v Composition, Percent (Balance Titanium) 7 Welded Not Welded Not Welded Welded 4.4 1.5 Br 1.3 v 2.1 Br 2.0 5Sb-5Sn 4. 7 1. 5 B 1. 1 2.5sb- .5Sn 1.1 Y 2.2 Br 1.3 3.2 1.7 Br 1. 1 Sb 4. 9 2. 5 B 0. 8 12.5Sb-2.5Sn. 7.6 1.9 5.7 1.8 10Sb-5S 4.3 2.5 Br. 1.1 6.6 1.7 ,Br 1.5 2.5sb12.5sn 5. 7 2. 9 Br 0. 8 15sn 3.4 1.8 1.6 a 5% 2.4 1.5 Er 1.5 1.5 2.1 Br 1.3 4.2 1.5 Br 1.2 1.9 2.1 Br 2.8 5.2 2.7 11.6 2.8 4.4 1.5 Br 2.7 1.9 2.1 Br 1.7 5.2 2.5 Br 1.5 2.9 2.8 Br 7 1.2 Br 2.5 Br 2.6 V Br 10. 6 1. 7 .5s 5. 8 2. 6 Br 1. 4 l2.5Sb-1Al 5. 8 2.1 7.1 2. 7 12.5Sb-2AL 2. 9 2.3 Br 3. 1 12.5Sb-3AL 7 Br Br 1. 7 15 4.9 v 2.5 5.3 1.9 7.6 3.1 11.0 2.9 V Br Br Er 5.9 V Br Br Br v1.6 7.3. Br 1 Br 1.6 V Br Br Br 2.5 5.7 2.8 Br 2.0 5.0 2.4 1.5 1.0 4.9 2.6 6.8 2.4 2.0 2.8 Br 2.5 7 2.6 10.6 1.7 8 2.5 9.6 1.5 vBr 2.0 6.6 -3.7 6.4 2.5 Br 2.5 8' -6.2 10.4 1.7 V Br 3.0 Br 9.4 v Br 5.5 7.0 2.3 2.8 2.8 0.5sb3 0Mo Br 0.9 5.7 2.8 0.5Sb,V 1. 8 0 3. 1 2. 1 0.5Sb+40V- 7. 1 0 2. 9 2. 9 0.5Sb3OTa 0.5 0. 5 2. 8 2. 8 0.5Sb-300b 0. 5 0. 9 3. 8 2,. 9 0.5Sb-30Zr Br 6. 0 5.5 2.8

5.2 2.8 v y 7.3. 2.8 i From the above; d-atait w ll be. seen that. the alloys, of r. V Br 2.8

L9 the invention 1n general suffer no appreciable loss 1n 8 ductility as a result of welding. i 1 1:7 The beta-containing; alloys of the invention after being i-g given the stabilizing treatment of Table V, are quite 0 0.4 stable thermally as shownby agingtests earned out at g-g 400 C. for 48 hours, which are shown to have substanzlg :3 tially no effect on the minimum bend ductilities. g f 8 5.5 The alloys of the invention may be made by melt cast- 0 0 ing in a cold mold furnace employing an arc electrode 5 i-g in an inert atmosphere, or by other procedures. Where 1:0 '0 the alloys of the invention are to be used for sheet mateg ria'l, the minimum bend ductility may range as high'as Br 3.5 20T, and where used in massive-form, as in forgings, the 2:3. 3 percent tensileelongati-on may range as flow as 1 or 2%.

g-g What is claimed isz V Br 0: 9 1. A titanium base alloy consisting essentially of: about g; 1:; 0.5 to 18% antimony; carbon, oxygen and nitrogen up to -g 8-: about 0.6%,.-.0.4%' 'and 0.3% 'each, respectively; about 1 0.5 'to 23% of at leastone other alpha promoter selected g-g from the group consisting of aluminum, tin, indium, silver, Br 8:4 lead and bismuth, but not to exceed 8% of aluminum and g; 2:} 15% in total amount of indium, silver, lead and bismuth; 3 antimony being on the low side of its range when said B; 1 11 other alpha promoter content is on the high side of its g; 2'2 range and vice versa; the balance of said alloy being sub- Br 1014 st-antially titanium, said alloy being characterized by at 148134 g; tensile strength of at least 100,000 p. s. ,i., a tensile elong 19 tion of at least 2% and a minimum'bend ductility of at least 20T.

2. A titaniumbase alloy consisting essentially of: about 0.5 to 18% antimony; carbon, oxygen and nitrogen up to' about 0.6%,0.4%' and 0.3% each, respectively; 0.5 to 40% of at least one beta promoter selected from the group'consisting of molybdenum, vanadium, columbium, tantalum, zirconium, manganese, iron, chromium, tungsten, cobalt, nickel, copper, silicon and beryllium, but not to exceed about 25% of chromium and tungsten, 10% of manganese, 7% of iron, 5% of cobalt, nickel and copper, and 2% of silicon and beryllium; the balance of said al loy being substantially titanium, and said alloy being characterized by a tensile strength of at least 100,000 p. s. i., a tensile elongation of at least 2% and a minimum bend ductility of at least 20T.

3. A titanium base alloy consisting essentially of: about 0.5 to 18% antimony; carbon, oxygen and nitrogen up to about 0.6%, 0.4% and 0.3% each, respectively; 0.5 to 40% of at least one beta promoter selected from the group consisting of molybdenum, vanadium, columbium, tantalum, zirconium, manganese, iron, chromium, tungsten, cobalt, nickel, copper, silicon and beryllium, but not to exceed about 25% of chromium and tungsten, of manganese, 7% of iron, 5% of cobalt, nickel and copper, and 2% of silicon and. beryllium; 0.25 to.23% of at least one other alpha promoter selected from the group consisting of tin, aluminum, indium, silver, lead and bismuth, but not to exceed 8% aluminum and in total amount of indium, silver, lead and bismuth; the balance of vsaid alloy being substantially titanium, and said alloy being characterized by 'a tensile strengthof at least 100,000 p. s. i., a tensile elongation of at least 2%, and a minimum bend ductility of at least T.

4. A titanium base alloy consisting essentially of: about 1 to 18% antimony about 0.5 to 40% of at least one beta-promoting element selected from the group consisting of molybdenum, vanadium, columbium, zirconium and tantalum, carbon up to about 0.6%, oxygen up to about 0.4%, nitrogen up to about 0.3%, characterized in having a beta-containing microstructure, a minimum bend ductility of not over 20T, and an ultimate strength at least 10% in excess of the titanium-base metal.

5. A titanium base alloy consisting essentially of: from more than 5 to about 18% antimony and about 0.25 to 5% aluminum in which the maximum antimony content is related to the aluminum content as follows:

Percent Maximum Aluminum Percent Antimony said alloy containing up to about 0.6% carbon, up to about 0.4% oxygen, up to about 0.3% nitrogen, char- 20, 23% of at least one other alpha-promoting element including aluminum under 3.5%, characterized in having a minimum bend-ductility of not over 20T and an ultimate strength at least 10% inexce ss of the unalloyed titanium-base metal.

7. An alloy consisting of: about 1 to 18% antimony, up to about 0.6% carbon, up to about 0.4% oxygen, up to about 0.3% nitrogen, balance titanium.

8. A titanium base alloy consisting essentially of: about 1 to 18% antimony, up to about 0.6% carbon, up to about 0.4% oxygen, up to about 0.3% nitrogen, under 3.5% aluminum, up to about 22% tin, the maximum tin content being related to the antimony content in accordance with the folowing tabulation:

Percent Percent Sb Sn Max.

chromium and tungsten, characterized in having a minimum 'bend ductility not over 20T, and an ultimate strength at least 10% in excess of the unalloyed titanium-base metal.

10. A titanium base alloy consisting essentially of: about 1 to 18% antimony, up to about 0.6% carbon, up to about 0.4% oxygen, up to about 0.3% nitrogen, about 0.5 to 10% manganese, characterized in having a minimum bend ductility not over 20T, and an ultimate strength at least 10% in excess of the unalloyed titaniumbase metal.

' 11. A titanium base alloy consisting essentially of: about 1 to 18% antimony, up to about 0.6% carbon, up to about 0.4% oxygen, up to about 0.3% nitrogen, about 0.5 to 7.5% iron, characterized in having a minimum bend ductility not over 20T, and an ultimate strength at least 10% in excess of the unalloyed titanium-base metal.

12. A titanium base alloy consisting essentially of: about 1 to 18% antimony, up to about 0.6% carbon, up to about 0.4% oxygen, up to about 0.3% nitrogen, about 0.5 to 5% of metal selected from the group consisting of copper, nickel and cobalt, characterized in having a minimum bend ductility not over 20T, and an ultimate strength at least 10% in excess of the unalloyed titaniumbase metal.

References Cited in the file of this patent UNITED STATES PATENTS 2,554,031 Iaifee May 22, 1951 2,596,487 I-aifee May 13, 1952 2,669,514 Finaly Feb. 16, 1954 OTHER REFERENCES Journal of Metals, March 1950, pages 498-499. 

1. A TITANIUM BASE ALLOY CONSISTING ESSENTIALLY OF: ABOUT 0.5 TO 18% ANTIMONY; CARBON, OXYGEN AND NITROGEN UP TO ABOUT 0.6%, 0.4% AND 0.3% EACH, RESPECTIVELY; ABOUT 0.5 TO 23% OF AT LEAST ONE OTHER ALPHA PROMOTER SELECTED FROM THE GROUP CONSISTING OF ALUMINUM, TIN, INDIUM, SILVER, LEAD AND BISMUTH, BUT NOT TO EXCEED 8% OF ALUMINUM AND 15% IN TOTAL AMOUNT OF INDIUM, SILVER, LEAD AND BISMUTH; ANTIMONY BEING ON THE LOW SIDE OF ITS RANGE WHEN SAID OTHER ALPHA PROMOTER CONTENT IS ON THE HIGH SIDE OF ITS RANGE AND VICE VERSA; THE BALANCE OF SAID ALLOY BEING SUBSTANTIALLY TITANIUM, SAID ALLOY BEING CHARACTERIZED BY A TENSILE STRENGTH OF AT LEAST 100,000 P.S.I., A TENSILE ELONGA- 